CN114250413A - Tempering-free hot-rolled Gepa-grade high-strength steel and production method thereof - Google Patents
Tempering-free hot-rolled Gepa-grade high-strength steel and production method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention provides a conditioning-free hot-rolled Gipa-grade high-strength steel and a production method thereof, wherein the high-strength steel comprises the following chemical components in percentage by weight: 0.14 to 0.20 percent of C, 0.10 to 0.20 percent of Si, 1.80 to 2.40 percent of Mn, less than 0.02 percent of P, less than 0.01 percent of S, 0.50 to 0.70 percent of Als, 0.020 to 0.04 percent of Nb, and 0.020 to 0.04 percent of Ti; the others are Fe and inevitable trace impurities; the production process comprises the working procedures of steel making, continuous casting, slab heating, controlled rolling, controlled cooling, coiling and warehousing slow cooling. The invention obtains the lath martensite + lath bainite + massive ferrite + residual austenite four-phase structure high-strength steel through the component design, controlled rolling and cooling processes, and the obtained high-strength steel has the characteristics of high extensibility, high toughness, high strength and high wear resistance.
Description
Technical Field
The invention relates to a method for producing conditioning-free hot-rolled Gipa-grade high-strength steel based on TRIP effect.
Background
Due to the national requirements of load limitation and environmental protection, the requirements for the load, light weight and fuel consumption of dump trucks, mixer trucks and the like are continuously increased, so that the steel plate with low cost, high extensibility, high toughness, high strength and high wear resistance is urgently needed to be provided.
The Gipag grade high-strength steel has the characteristics of low cost, high extensibility, high toughness, high strength and high wear resistance, and is widely applied to the field of engineering machinery. The traditional hot continuous rolling high-strength steel has the highest strength of only about 800MPa and high alloy cost, and the Gipa high-strength steel is mainly obtained by offline quenching and tempering heat treatment after rolling, so that the problems of long process flow, high process cost, long delivery cycle and the like exist.
The patent CN106148822A discloses 'a thick steel plate with low yield ratio, high strength and toughness and excellent low-temperature impact toughness and a manufacturing method thereof', which comprises the following chemical components in percentage by weight: c: 0.05-0.10, Si: 0.15-0.35, Mn: 1.0-1.8, P <0.014, S <0.001, Nb: 0.03-0.05, Ti: 0.0012-0.02, Ni: 0.5-1.0, Cr: 0.1-0.4, Cu: 0.5-1.0, Mo: 0.1-0.5, Alt: 0.001-0.03, and the balance of iron and inevitable impurities; the on-line quenching and high-temperature tempering process is adopted, the process is complex, the process and the alloy cost are high, the delivery period is long, and only thick plates can be produced.
The CN108411203A patent discloses 'NM 300 wear-resistant steel for a high-silicon high-aluminum concrete mixer and a production method thereof', and the steel comprises the following chemical components in percentage by weight: c = 0.10-0.16, Si = 1.0-1.50, Mn = 1.50-2.0, P ≤ 0.015, S ≤ 0.005, Nb = 0.010-0.060, Ti ≤ 0.030, Al = 0.4-0.6, and the balance of Fe and other unavoidable impurities, wherein the carbon equivalent CEV of the wear-resistant steel is ≤ 0.52%; the surface red embroidery with high Si content is serious, the final material structure is a ferrite and martensite dual-phase structure, and the elongation A50 is as low as 8 percent.
Disclosure of Invention
The invention aims to solve the technical problem of providing a conditioning-free hot-rolled Gipa-grade high-strength steel and a production method thereof, and the conditioning-free hot-rolled Gipa-grade high-strength steel has the characteristics of low cost, high extensibility, high toughness, high strength, high wear resistance and quick delivery.
The technical scheme for solving the technical problems is as follows:
the conditioning-free hot-rolled Gipa-grade high-strength steel comprises the following main chemical components in percentage by weight: 0.14 to 0.20 percent of C, 0.10 to 0.20 percent of Si, 1.80 to 2.40 percent of Mn, less than 0.02 percent of P, less than 0.01 percent of S, 0.50 to 0.70 percent of Als, 0.020 to 0.04 percent of Nb, and 0.020 to 0.04 percent of Ti; the others are Fe and inevitable trace impurities.
The conditioning-free hot-rolled Gipa-grade high-strength steel adopts a proper C content in the aspect of component design, and simultaneously adds Mn, Als, Nb, Ti and a small amount of Si alloy.
C: as interstitial atoms in steel, it is very important to improve the strength of steel. Too low C content does not guarantee sufficient strength of the steel and affects C partitioning, while too low C content affects phase stability of the retained austenite at room temperature; while excessive C content makes ferrite precipitation difficult and deteriorates weldability. Therefore, the content of C is limited to 0.14-0.20 percent in the invention.
Mn: mn is an important element for expanding an austenite phase region, can reduce the critical quenching speed of steel and postpones the transformation from austenite to pearlite; meanwhile, the Ms point in the steel can be reduced, the austenite is stabilized, and the proper phase stability of the residual austenite is ensured. Too low a Mn content is insufficient to stabilize a sufficient content of austenite in the critical region and reduces the phase stability of the retained austenite at room temperature, resulting in work hardening behavior of the steel; meanwhile, excessive Mn is easy to form serious center segregation and damage the uniformity of the structure. Therefore, the Mn content is limited to 1.80-2.40 percent
Si: si is an element for promoting ferrite to generate, and simultaneously, carbon can be prevented from being precipitated in the form of carbide in the distribution process, so that conditions are provided for diffusion of carbon atoms in the distribution process, and local enrichment of carbon is promoted. Meanwhile, Si acts as a deoxidizer to reduce the aluminum consumption. However, adding too much Si reduces the surface quality of the steel. Therefore, the Si content in the present invention is controlled to be 0.10 to 0.20 wt%.
Al: al is one of important elements in the steel plate, Al is a deoxidizer in the steel-making process in the traditional process, and meanwhile, Al can be combined with N in steel to form AlN and refine grains. Therefore, the Al content is limited to be 0.5-0.7 percent in the invention.
Nb: the invention adopts trace Nb component design: firstly, Nb can refine grains and improve the strength of the high-strength steel; and secondly, high-content retained austenite is obtained, and the Nb element can also improve the stability of the retained austenite in the steel.
Ti: in the composition, Ti is mainly used for fixing N. Ti and N form TiN at high temperature, and the TiN can inhibit austenite grains from growing when the slab is heated to austenitize; ti and C form TiC at a lower temperature range, and fine TiC particles are beneficial to improving the low-temperature toughness of the steel plate. If the Ti content is too high, coarse square TiN precipitates are formed, and the low-temperature toughness is reduced. Therefore, the Ti content in the present invention is controlled to be in the range of 0.02 to 0.04%.
The invention also provides a production method of the conditioning-free hot-rolled Gipa-grade high-strength steel, which comprises the working procedures of steel making, slab continuous casting, heating, controlled rolling, controlled cooling, coiling and warehousing slow cooling.
In the continuous casting process, pure molten steel obtained by smelting is subjected to dynamic soft reduction technology, the total reduction amount is 5-7mm, and the component segregation and the center porosity of a casting blank are reduced.
The rolling process is controlled, and 3+5 passes of rough rolling are adopted; the finish rolling temperature is set to be 840-870 ℃.
The control cooling process adopts sectional cooling, and ultra-fast cooling is adopted at a cooling speed of 90-200 ℃/s at one section; the middle air cooling time is 11-16s, and the air cooling temperature is 700-; the cooling second section adopts layer cooling with the cooling speed of 40-55 ℃/s; coiling after the second-stage cooling is finished
The coiling process has the coiling temperature of 310-360 ℃; and (4) after coiling, warehousing and slowly cooling, wherein the average slow cooling speed is less than 0.5 ℃/min.
The thickness of the high-strength steel strip is 2.5-8 mm.
The high-strength steel is obtained based on the TRIP effect.
The production method of the conditioning-free hot-rolled Gipa-grade high-strength steel comprises the following steps of:
selection of finishing temperature in the refining process: adopting a Gleeble3500 thermal simulation test to obtain an austenite continuous cooling transformation curve of the conditioning-free hot-rolled high-strength steel, obtaining that the temperature of a double-phase region is 691-768 ℃, considering reducing the deformation resistance of finish rolling and avoiding rolling of the double-phase region, and setting the lower limit of the finish rolling temperature to 840 ℃; the upper limit of the finish rolling temperature is set to 870 deg.c in consideration of the fine grain strengthening effect of Nb and the retained austenite stability and content.
Selection of air cooling temperature: considering that the temperature of the two-phase zone is 691-768 ℃, the upper limit of the air cooling temperature is 760 ℃, the lower limit of the air cooling temperature is 700 ℃, and the ferrite generated in the two-way zone is quasi-polygonal block-shaped ferrite, so that the ductility is better.
Selection of air cooling time: in order to obtain a certain proportion of ferrite, high strength and certain ductility and toughness are ensured, and the intermediate air cooling time is set to be 11-16 s.
And (3) selecting the sectional cooling speed: the cooling section adopts ultra-fast cooling, the cooling speed is set to be 90-200 ℃/s, and the austenite rapidly enters a ferrite-austenite bidirectional phase transition region; and the cooling second stage adopts layer cooling, the cooling speed is set to be 40-55 ℃/s, so that the coiling temperature is easy to control, a certain amount of bainite is generated, and pearlite is prevented from being generated.
Selection of coiling temperature: obtaining that the MS point of the conditioning-free hot-rolled high-strength steel is 440-386 ℃ by adopting a Gleeble3500 thermal simulation test; in order to obtain martensite to ensure the strength and hardness of the steel sheet, the upper limit of the coiling temperature is set to 360 ℃, and in order to obtain a certain content of residual austenite to ensure the TRIP effect, the lower limit of the coiling temperature is set to 310 ℃.
And (3) warehousing and slow cooling after coiling: the average slow cooling speed is less than 0.5 ℃/min, and the steel plate can release the residual stress of the steel plate after coiling and put in storage for slow cooling, and promote the distribution of C, thereby ensuring the content and stability of the residual austenite.
Adopt the produced beneficial effect of above-mentioned technical scheme to lie in:
the invention adopts the hot continuous rolling quality-adjustment-free technology, the cost is low, and the delivery is fast; the produced high-strength steel has a four-phase structure of lath martensite, lath bainite, massive ferrite and residual austenite, the content of residual austenite is greater than 7.5%, the elongation is greater than 20%, the tensile strength is greater than 1000MPa, the bending diameter d =3a (a is the thickness of the steel plate) is cold-bent at 180 degrees and has no crack, and the impact energy at-40 ℃ is greater than 110J.
Drawings
FIG. 1 is a metallographic structure diagram of a hot-rolled high-strength steel free of quenching and tempering obtained in example 1;
FIG. 2 is a metallographic structure diagram of a hot-rolled high-strength steel free of quenching and tempering obtained in example 2;
FIG. 3 is a metallographic structure diagram of a hot-rolled high-strength steel free of quenching and tempering obtained in example 3;
FIG. 4 is a metallographic structure chart of a hot rolled high strength steel free of quenching and tempering obtained in example 4;
FIG. 5 is a metallographic structure diagram of a hot-rolled high-strength steel free of quenching and tempering obtained in example 5;
FIG. 6 is a metallographic structure chart of a hot-rolled high-strength steel free of quenching and tempering obtained in example 6.
Detailed Description
The technical solution of the present invention will be further described below by way of specific examples.
The quality-adjustment-free hot-rolled high-strength steel provided by the invention is produced by adopting a top-bottom combined blown converter, an LF (ladle furnace), an RH (RH) ladle refining furnace, a two-machine double-flow slab caster, a digital combustion technology heating furnace, a two-machine frame four-roller high-speed reversible rough mill set, a 7-machine frame four-roller strip steel finishing mill set and ultra-fast cooling and laminar cooling equipment.
The conditioning-free hot-rolled Gepa-grade high-strength steel comprises the following chemical components in percentage by weight: 0.14 to 0.20 percent of C, 0.10 to 0.20 percent of Si, 1.80 to 2.40 percent of Mn, less than 0.02 percent of P, less than 0.01 percent of S, 0.50 to 0.70 percent of Als, 0.020 to 0.04 percent of Nb, and 0.020 to 0.04 percent of Ti; the others are Fe and inevitable trace impurities.
The production method of the conditioning-free hot-rolled Gipa-grade high-strength steel comprises the working procedures of steel making, slab continuous casting, heating, controlled rolling, controlled cooling, coiling and warehousing slow cooling. Wherein, the rolling procedure is controlled, and the finish rolling temperature is set to be 840-870 ℃; controlling a cooling process, adopting sectional cooling, and adopting ultra-fast cooling at a cooling speed of 90-200 ℃/s at the first section of cooling; the middle air cooling time is 11-16s, and the air cooling temperature is 700-; the cooling second section adopts layer cooling with the cooling speed of 40-55 ℃/s; a coiling step, wherein the coiling temperature is set to be 310-360 ℃; and warehousing and slow cooling, wherein the average slow cooling speed is less than 0.5 ℃/min, and the thickness of the produced high-strength steel strip is 2.5-8 mm.
Table 1 shows the chemical compositions and weight percentages of the conditioning-free hot rolled high strength steels provided in examples 1-6.
Table 1 chemical composition of high strength steel in each example, wt%
Specific process parameters for examples 1-6 are shown in Table 2; the main performance test results of the produced high-strength steel are shown in table 3.
Table 2 production process parameters of high strength steel of each example
Table 3 performance test results of high-strength steel of each example
As can be seen from Table 3, the invention can realize the production of the conditioning-free hot-rolled high-strength steel by the combined control of components and processes, the average extension of the produced conditioning-free hot-rolled high-strength steel reaches 24.4 percent, the average tensile strength reaches 1077MPa, the bending diameter d =3a (a is the thickness of the steel plate), no crack exists when the steel plate is cold-bent at 180 degrees, and the average impact energy reaches 145.5J at-40 ℃.
Metallographic structures of conditioning-free hot rolled high strength steels produced in examples 1 to 6 are shown in FIGS. 1 to 6. As can be seen from fig. 1 to 6, the texture of the conditioning-free hot-rolled gigapascal grade high-strength steel provided by the invention is a four-phase texture of lath martensite + lath bainite + massive ferrite + residual austenite, wherein the lath martensite + lath bainite contributes to the strength of the steel plate, and the massive ferrite and the residual austenite provide ductility and toughness for the steel plate, and the residual austenite is transformed into martensite during the processing process, so that the plasticity, toughness, strength and hardness of the steel plate are further enhanced.
Claims (7)
1. A conditioning-free hot-rolled Gipa-grade high-strength steel is characterized in that: the high-strength steel comprises the following chemical components in percentage by weight: 0.14 to 0.20 percent of C, 0.10 to 0.20 percent of Si, 1.80 to 2.40 percent of Mn, less than 0.02 percent of P, less than 0.01 percent of S, 0.50 to 0.70 percent of Als, 0.020 to 0.04 percent of Nb, and 0.020 to 0.04 percent of Ti; the others are Fe and inevitable trace impurities.
2. The temper-free hot rolled gipa-grade high strength steel as claimed in claim 1, wherein the thickness of the high strength steel strip is 2.5-8 mm.
3. A method for producing the temper-free hot rolled Gipa grade high strength steel as claimed in claim 1 or 2, comprising the working procedures of steel making, slab continuous casting, heating, controlled rolling, controlled cooling, coiling, warehousing and slow cooling; the method is characterized in that: the control cooling process adopts sectional cooling, and the ultra-fast cooling is adopted at the first cooling section, wherein the cooling speed is 90-200 ℃/s; the middle air cooling time is 11-16s, and the air cooling temperature is 700-; and the cooling second section adopts layer cooling with the cooling speed of 40-55 ℃/s.
4. The method for producing the temper-free hot-rolled gipa-grade high-strength steel as claimed in claim 3, wherein the rolling process is controlled, and the finish rolling temperature is set to 840 ℃ to 870 ℃.
5. The method for producing a temper-free hot rolled Gipa grade high strength steel as claimed in claim 3, wherein the coiling temperature is set to 310-360 ℃.
6. The method for producing the temper-free hot-rolled Gipa grade high strength steel according to claim 3, wherein in the warehousing slow cooling process, the average slow cooling speed is less than 0.5 ℃/min.
7. The method for producing temper-free hot rolled Gipag grade high strength steel according to any one of claims 3 to 6, wherein the Gipag grade high strength steel produced by the method is lath martensite + lath bainite + massive ferrite + residual austenite four-phase structure.
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| CN113522988A (en) * | 2021-06-21 | 2021-10-22 | 武汉钢铁有限公司 | Control method for shape of thin-specification ultrahigh-strength steel plate in DQ (data-from-data) process |
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